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WO2007108180A1 - Alliage a memoire de forme haute temperature, actionneur et moteur associes - Google Patents

Alliage a memoire de forme haute temperature, actionneur et moteur associes Download PDF

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Publication number
WO2007108180A1
WO2007108180A1 PCT/JP2006/324206 JP2006324206W WO2007108180A1 WO 2007108180 A1 WO2007108180 A1 WO 2007108180A1 JP 2006324206 W JP2006324206 W JP 2006324206W WO 2007108180 A1 WO2007108180 A1 WO 2007108180A1
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WO
WIPO (PCT)
Prior art keywords
mol
alloy
temperature
shape memory
memory alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2006/324206
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English (en)
Japanese (ja)
Inventor
Shuichi Miyazaki
Heeyoung Kim
Yoshinari Takeda
Masanari Tomozawa
Buenconsejo Pio
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University of Tsukuba NUC
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University of Tsukuba NUC
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by University of Tsukuba NUC filed Critical University of Tsukuba NUC
Priority to JP2008506165A priority Critical patent/JP4910156B2/ja
Priority to EP06833961A priority patent/EP1997922B1/fr
Publication of WO2007108180A1 publication Critical patent/WO2007108180A1/fr
Anticipated expiration legal-status Critical
Priority to US12/235,528 priority patent/US20090218013A1/en
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/006—Resulting in heat recoverable alloys with a memory effect
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02K—JET-PROPULSION PLANTS
    • F02K1/00—Plants characterised by the form or arrangement of the jet pipe or nozzle; Jet pipes or nozzles peculiar thereto
    • F02K1/54—Nozzles having means for reversing jet thrust
    • F02K1/76—Control or regulation of thrust reversers
    • F02K1/763—Control or regulation of thrust reversers with actuating systems or actuating devices; Arrangement of actuators for thrust reversers
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
    • F03G—SPRING, WEIGHT, INERTIA OR LIKE MOTORS; MECHANICAL-POWER PRODUCING DEVICES OR MECHANISMS, NOT OTHERWISE PROVIDED FOR OR USING ENERGY SOURCES NOT OTHERWISE PROVIDED FOR
    • F03G7/00—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for
    • F03G7/06—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like
    • F03G7/061—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element
    • F03G7/0614—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element using shape memory elements
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
    • F03G—SPRING, WEIGHT, INERTIA OR LIKE MOTORS; MECHANICAL-POWER PRODUCING DEVICES OR MECHANISMS, NOT OTHERWISE PROVIDED FOR OR USING ENERGY SOURCES NOT OTHERWISE PROVIDED FOR
    • F03G7/00—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for
    • F03G7/06—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like
    • F03G7/061—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element
    • F03G7/0616—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element characterised by the material or the manufacturing process, e.g. the assembly
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/04—Heavy metals
    • F05C2201/0433—Iron group; Ferrous alloys, e.g. steel
    • F05C2201/0466—Nickel
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/90—Alloys not otherwise provided for
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2300/00—Materials; Properties thereof
    • F05D2300/50—Intrinsic material properties or characteristics
    • F05D2300/505—Shape memory behaviour

Definitions

  • the present invention relates to a high-temperature shape memory alloy that can be used at a high temperature of 100 ° C or higher and an actuator motor using the shape memory alloy, and in particular, a martensitic transformation peak temperature or a reverse transformation peak temperature.
  • the present invention relates to a high-temperature shape memory alloy having a temperature of 100 ° C. or higher and an actuator using the shape memory alloy.
  • a Ti—Ni—Cu alloy (Patent Document 1 (JP 2002-294371 A)) having an expression temperature of shape memory characteristics in a range of 200K to 360K is known. Yes. Also known is a Ti—Ni—Nb-based alloy (Patent Document 2 (Patent No. 2539786)) having a martensite transformation start temperature (Ms) as low as 50 ° C. or lower.
  • the following alloys are conventionally known as high-temperature shape memory alloys that can be used as shape memory alloys in a high-temperature environment of 100 ° C or higher by adding other elements to the TiNi-based alloy. .
  • Titanium (Ti) is replaced with 0 to 20 mol% hafnium (Hf), and (Ti—Hf) —Ni alloys achieve 373 (K) ⁇ Ms 560 (K). [0004] (3) Ti— (Ni— Pd) alloy
  • a Ti— (Ni—Pd) alloy in which nickel (Ni) is replaced with O to 50 mol% palladium (Pd) achieves 280 (K) ⁇ Ms ⁇ 800 (K)!
  • Ti- (Ni-Pt) alloys in which nickel (Ni) is replaced with 0-50 mol% platinum (Pt) can achieve 280 (K) and Ms 1300 (K)!
  • a Ni-A1 alloy consisting of 30-36mol% aluminum (A1) and the remaining nickel (Ni) realizes 273 (K) and Ms and 1000 (K)!
  • a Ti—Nb alloy consisting of 10 to 28 mol% of niobium (Nb) and the balance of titanium (Ti) achieves 173 (K) ⁇ Ms 900 (K).
  • Patent Document 3 describes a Ti—Pd-based alloy with 48at% to 50at% palladium (Pd) and 50at% to 52at% Ti, and a reverse transformation end temperature (Af) of 560 ° C (833K) or higher. Is described.
  • Non-Patent Document 1 describes an alloy having 50 mass% (less than 30 mol% in terms of mol%) tantalum (Ta) and the balance Ti, or 4 mass% tin (Sn) or lOma ss in Ti-Ta. It is described that a shape recovery start temperature of 150 ° C. (423 K) or more can be realized by an alloy in which% zirconium (Zr) is mixed and melted.
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2002-294371
  • Patent Document 2 Japanese Patent No. 2539786
  • Patent Document 3 Japanese Patent Laid-Open No. 11-36024
  • the conventional shape memory alloys (1) and (2) that can be used at high temperatures are prone to brittle cracking, and thus have a problem that they cannot be freely cured by molding or the like with poor workability.
  • the shape memory alloy (6) forms a precipitate (Ni A1) that is not only workable but also has poor structural stability and causes embrittlement. Therefore, it cannot be repeatedly used at 200 ° C or higher.
  • the workability is good, but the structural stability is poor.
  • the transformation temperature is lowered because the ⁇ phase is formed which causes the loss of shape memory characteristics.
  • the shape memory alloy (9) has a problem that it cannot be repeatedly used because it is easily plastically deformed. Another problem is that the shape memory characteristics are lost as soon as the ⁇ phase is formed during use.
  • the present inventor focused on the prior arts (1) and (2) showing shape memory characteristics at high temperatures, and conducted experiments to improve the workability of Ti—Ni—Zr alloys and Ti—Ni—Hf alloys. , Earnestly research! I came to make the present invention described below.
  • the present invention has a first technical problem to provide a shape memory alloy that has high workability and can be used repeatedly at high temperatures.
  • the high temperature shape memory alloy of the first invention is
  • the total transformation temperature of 34.7 mol% to 48.5 mol% nickel, zirconium and hafnium is 6.8 mol% to 22.5 mol%. It has a workability improving additive element in which the total of niobium and tantalum is 1 mol% or more and 30 mol% or less, boron of 2 mol% or less, and the balance of titanium. (Transformation peak temperature (M *) or reverse transformation peak temperature (A *)) can be achieved, and the rolling rate in cold working can be improved. As a result, it is possible to provide a high-temperature shape memory alloy that can be used repeatedly at a high temperature, and to improve cold weatherability.
  • boron 2 mol% or less of boron is used to mean “Omol% of boron”, that is, including boron in some cases.
  • the high temperature shape memory alloy of the first aspect of the first invention is the first invention
  • the transformation temperature increasing additive element composed of 3 mol% or more and 30 mol% or less of niobium, It is characterized by including.
  • the high-temperature shape memory alloy of Form 1 of the first invention having the above-described constituents has 6.8 mol% to 22.5 mol% of zirconium and 3 mol% to 30 mol% of niobium.
  • a reverse transformation peak temperature (A *) of ° C or higher can be realized, and cold working can be performed at a high rolling rate.
  • the high-temperature shape memory alloy of Form 2 of the first invention is the first invention
  • the transformation temperature increasing additive element composed of 8 mol% or more and 18 mol% or less of hafnium
  • the high-temperature shape memory alloy of Form 2 of the first invention having the above-mentioned constituent elements has 6.8 mol% or more and 18 mol% or less hafnium and 3 mol% or more and 20 mol% or less niobium.
  • the reverse transformation peak temperature (A *) described above can be realized, the rolling rate can be improved, and cold caloeing can be achieved.
  • the high-temperature shape memory alloy of Form 3 of the first invention is the above-mentioned first invention
  • the cachetability improving additive element composed of 3 to 30 mol% of tantalum
  • the high-temperature shape memory alloy of Form 2 of the first invention having the above-described constituent elements is composed of 6.8 mol% or more and 20 mol% or less of the transformation temperature increasing additive element and 3 mol% or more and 30 mol% or less of tantalum. And an additive element for improving the caulking property. Compared with the case where it does not, workability can be improved.
  • the high-temperature shape memory alloy of Form 4 of the first invention is any one of the first invention to the form 3 of the first invention.
  • the ratio of total mol% of titanium, zirconium and hafnium divided by mol% of nickel is 0.98 or more and 1.14 or less.
  • the ratio obtained by dividing the total mol% of titanium, zirconium and hafnium by mol% of nickel is 0.98 or more 1.14 Therefore, the reverse transformation peak temperature (A *) of 100 ° C or higher can be realized, and cold working can be performed at a high V and rolling rate.
  • the actuator of the second invention is:
  • the high temperature shape memory alloy according to any one of the first invention or the first to fourth aspects of the first invention is used.
  • the actuator according to the second invention having the above-described constituent elements is composed of the high-temperature shape memory alloy according to any one of the first invention or the first to fourth aspects of the first invention, it can be processed by cold working. It has a high transformation temperature and shape memory characteristics, and can be used in high temperature environments.
  • the engine of the third invention is:
  • a flow rate adjusting valve constituted by the high temperature shape memory alloy according to any one of the first invention or the first to fourth aspects of the invention is provided.
  • the engine according to the third aspect of the present invention having the above-described constituent elements is provided with a flow rate adjusting valve composed of the high-temperature shape memory alloy according to any one of the first aspect or the first aspect of the first aspect of the invention. It has transformation temperature and shape memory characteristics and can be used under high temperature environment. The invention's effect
  • the present invention described above can provide a shape memory alloy that has high workability and can be used repeatedly at high temperatures.
  • FIG. 1 is an explanatory view of an image obtained by observing an alloy 7 of an example of the present invention with a scanning electron microscope.
  • FIG. 2 is an explanatory view of an image obtained by observing the alloy 8 of the example of the present invention with a scanning electron microscope.
  • test pieces of Alloy 1 to Alloy 55 having the alloy compositions shown in Table 1 to Table 10 below were prepared and tested.
  • the test piece used for the experiment was prepared by the following methods (1) to (3).
  • Alloy 2 (Ti—Ni—Zr) is composed of 49.5 mol% Ni and 10 mol% Zr.
  • the workability of the alloy produced by the production method was evaluated by conducting a workability evaluation test.
  • cold rolling was performed to a rolling rate of 60% using a cold rolling mill. Samples fractured until the rolling rate reached 60% were evaluated for workability by measuring the rolling rate at the time of fracture.
  • the transformation temperature of each alloy was determined by heat treatment of the cold-rolled material at 700 ° C for 1 hour, and the martensitic transformation peak temperature (DSC) by differential scanning calorimetry (DSC). Point) and reverse transformation peak temperature (A * point).
  • the composition of the conventionally known Ti-Ni-Zr ternary alloys Alloy 1 to Alloy 4 the total mol% of Ti and Zr divided by mol% of Ni, and the ratio of nickel to fracture Table 1 shows the rolling ratio (%), martensitic transformation peak temperature (M * point, ° C) and reverse transformation peak temperature (A * point, ° C).
  • Examples of the present invention include the composition of alloys 5 to 7 of a quaternary alloy of TiNi-Zr-Nb, the ratio of nickel to mol, and the total mol% of Ti and Zr divided by mol% of Ni.
  • Table 2 shows the rolling ratio (%), martensitic transformation peak temperature (M * point, ° C) and reverse transformation peak temperature (A * point, ° C).
  • Alloy 5, Alloy 6, and Alloy 7 are alloys having a component composition in which Ti and Zr components (mol%) of Alloy 3 are fixed and Ni is replaced with Nb.
  • the composition of Ti—Ni—Zr—Nb quaternary alloy 8 to alloy 12 and the total mol% of Ti and Zr were divided by mol% of Ni.
  • Table 3 shows the ratio to nickel, rolling ratio (%) at break, martensitic transformation peak temperature (M * point), and reverse transformation peak temperature (A * point).
  • Alloys 8 to 12 are alloys in which the component ratios of Ti, Ni, and Zr are fixed to 35.5 mol%, 49.5 mol%, and 15 mol%, respectively, and the whole is substituted with Nb.
  • Examples and comparative examples of the present invention include Ti-Ni-Zr-Nb quaternary alloy 13 Alloy 17 composition, and the total mol% of Ti and Zr divided by mol% of Ni. Ratio, rolling ratio at break (%) Martensitic transformation peak temperature (M * point) and reverse transformation peak temperature (A * point) are shown in Table 4. Note that the transformation temperatures of Alloy 16 and Alloy 17 were not observed within the experimental range, and are considered to have become too low.
  • Examples and comparative examples of the present invention include Ti-Ni-Zr-Nb quaternary alloy 18 Alloy 26 composition and total nickel and Ti / Zr mol% divided by Ni mol% Ni Ratio, rolling ratio at break (%) Martensitic transformation peak temperature (M * point) and reverse transformation peak temperature (A * point) are shown in Table 5.
  • Examples and comparative examples of the present invention include compositions of alloys 27 to 37 of a quaternary alloy of Ti-Ni-Hf-Nb and a quaternary alloy of Ti-Ni-Zr-Hf-Nb, and Ti , The total mol% of Zr and Hf divided by mol% of Ni, the ratio to nickel, the rolling reduction at break (%), the martensite transformation peak temperature (M * point) and the reverse transformation peak temperature (A * point) Table 6 shows.
  • Alloy 28 and alloy 29 correspond to the alloy 9 and alloy 10 with Zr replaced with Hf
  • the alloy 30 corresponds to the alloy 20 with Zr replaced with Hf
  • Alloy 31 corresponds to the alloy 7 in which Zr is replaced with Hf.
  • Alloy 32 corresponds to half of Zr (10 mol%) in Alloy 19 replaced with Hf
  • Alloy 33 corresponds to half of Zr (15 mol%) in Alloy 9 replaced with Hf. . That is, in Alloys 32 and 33, the sum of Zr and Hf (additional element for improving transformation temperature) is 9 mol% and 12 mol%, respectively.
  • the composition of Ti-Ni-Zr-Ta quaternary alloy 38 to alloy 42 And the total mol% of Ti and Zr divided by mol% of Ni to the nickel ratio, rolling reduction at break (%), martensitic transformation peak temperature (M * point) and reverse transformation peak temperature (A * point) are shown in Table 7.
  • Alloys 38 to 42 are alloys in which the component ratios of Ti, Ni, and Zr are fixed to 40.5 mol%, 49.5 mol%, and 10 mol%, respectively, and the whole is replaced with Ta.
  • the composition of alloy 43 to alloy 48 which is a quaternary alloy of Ti-Ni-Zr-Ta and a quaternary alloy of Ti-Ni-Zr-Nb-Ta, and Ti, Zr Table 8 shows the total mol% divided by the mol% of Ni, the nickel-to-nickel ratio, the rolling reduction (%) at break, the martensitic transformation peak temperature (M * point), and the reverse transformation peak temperature (A * point).
  • Alloy 48 the total of Nb and Ta (additive element for improving strength) is 10 mol%.
  • Examples and comparative examples of the present invention include Ti-Ni-Zr-Nb-B quinary alloy alloys 49 to 52, and the total mol% of Ti and Zr divided by mol% of Ni.
  • Table 9 shows the ratio, rolling rate at break (%), martensitic transformation peak temperature (M * point), and reverse transformation peak temperature (A * point).
  • Alloys 49-52 are Ti-Ni-Zr-Nb alloys with B (boron) added. is there.
  • the composition of the alloy 53 to alloy 55 of Ti-Ni-Zr-Hf-Nb-Ta- ⁇ and the total mol% of Ti, Zr and Hf was changed to mol% of Ni.
  • Table 10 shows the nickel-to-nickel ratio divided by, the rolling rate at break (%), the martensitic transformation peak temperature (M * point), and the reverse transformation peak temperature (A * point).
  • FIG. 1 is an explanatory view of an image obtained by observing the alloy 7 of the example of the present invention with a scanning electron microscope.
  • Ti—Ni—Zr ternary alloys such as Comparative Examples 1 to 4 have a relatively low rolling ratio and poor workability. It can be seen that when zirconium (Zr, an element for increasing the transformation temperature) increases, the transformation temperature (M * point and A * point) increases, but the rolling rate decreases and the additive property decreases.
  • alloy 5 to alloy 7 in the example 5 in which Ni in the alloy 3 in the comparative example was replaced with Nb is a quaternary alloy of 1 ⁇ ⁇ -21: It can be seen that the rolling rate is improved and the workability is improved.
  • the transformation temperature (M *, A *) is also 100. Can be used under high temperature conditions of 100 ° C or higher. In particular, as the amount of Nb increases, the transformation temperature tends to decrease, but the transformation temperature changes little and the transformation temperature decreases rapidly. I knew that there wasn't.
  • Alloy 5 to Alloy 7 can be used under high temperature conditions and can be used as high temperature shape memory alloys with improved workability.
  • the rolling ratio up to breakage was improved, but it was observed that there were many fine forces and cracks.
  • the rolled alloy 7 has a soft and easily plastically deformed ⁇ phase and a hard and brittle Laves phase. The growth of cracks generated at the interface of the base phase is inhibited by the j8 phase, which improves workability.
  • FIG. 2 is an explanatory view of an image obtained by observing the alloy 8 of the example of the present invention with a scanning electron microscope.
  • the reverse transformation peak temperature (A *) is 100 even for the quaternary alloy of Ti—Ni—Zr—Nb in which the whole is replaced with Nb.
  • An alloy with a martensitic transformation peak temperature (M *) higher than C and a relatively high temperature could be realized.
  • Nb was 1 mol% (Comparative Example Alloy 11)
  • Nb was 3 mol% or more
  • the rolling ratio could be improved, especially when Nb was 10 mol% or more.
  • Alloy 9 ⁇ L 1 was able to achieve a rolling rate of 60% or more.
  • Alloy 8 ⁇ L 1, fine cracks were hardly formed compared to Alloys 5 ⁇ 7, and workability was improved.
  • the rolled alloy 8 has a soft calcium and ⁇ phase precipitated in the grain boundaries and in the grains, so that the workability is improved.
  • alloys 38 and 39 have a high transformation temperature when compared to the alloys 38 and 39 and the Nb-forced calendered alloys 18 and 19.
  • Alloys 43, 44, 46 when comparing Alloys 43, 44, 46 with Alloys 8, 9, 10, and Alloy 3, Alloys 43, 44, 46 to which Ta was added had a rolling reduction compared to Alloys 8 to 10 to which Nb was added. Although the improvement effect of is low, the rolling rate is improved compared to Alloy 3, and the transformation temperature can be higher than Alloy 8 to: LO added with Nb.
  • alloy 48 when alloy 48 is compared with alloys 44, 9 and alloy 3, alloy 48 with Ta and Nb added has a higher rolling reduction than alloy 44 with only Ta, and alloy 9 with only Nb. Compared with this, the transformation temperature can be increased.
  • Alloys 49 to 52 Nb was added to the Ti-Ni-Zr alloy, and B (boron, temperature 'workability improving additive element) was further added. As a result, it was confirmed that the rolling rate can be improved and the transformation temperature can be increased as compared with the case where B is not added (Alloy 8, Alloy 20).
  • Alloys 49, 50, 52 and Alloy 8 it can be seen that when mol% of B increases, the improvement effect tends to decrease, and it is desirable to add a small amount of mol% of B.
  • the shape memory alloy of the present invention is less likely to lose its shape memory characteristics even after repeated use under a high-temperature thermal cycle, so in an engine (automobile engine, aircraft engine, gas turbine) It can be used as a valve for gas flow paths that become hot, and it can be used to adjust the flow area by deformation due to the shape recovery effect during heating, and to return the flow area with a panel that deforms the valve during cooling. It is done. It can also be used as a valve to supply lubricant for a shaft that rotates at high speed. In addition, it can be applied to safety devices in hot parts such as the power supply of home appliances. It can also be used for an actuator used when working under high temperature conditions. When applied as an actuator, there is an advantage that the responsiveness is improved because the cooling rate is increased.

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  • Engineering & Computer Science (AREA)
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  • Combustion & Propulsion (AREA)
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  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Temperature-Responsive Valves (AREA)

Abstract

L'invention concerne un alliage à mémoire de forme présentant une excellente aptitude au façonnage et se prêtant à une utilisation répétée à haute température. Cet alliage à mémoire de forme haute température se caractérise en ce qu'il contient : des additifs augmentant la température de transformation contenant entre 34,7 et 48,5 % en moles de nickel et au moins du zirconium ou de l'hafnium, la somme de zirconium et d'hafnium étant comprise entre 6,8 et 22,5% en moles; des additifs améliorant l'aptitude au façonnage, contenant au moins du niobium ou du tantale, la somme de niobium et de tantale étant comprise entre 1 et 30% en moles; jusqu'à 2% en moles de bore; le reste étant constitué par du titane et des impuretés inévitables.
PCT/JP2006/324206 2006-03-20 2006-12-05 Alliage a memoire de forme haute temperature, actionneur et moteur associes Ceased WO2007108180A1 (fr)

Priority Applications (3)

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JP2008506165A JP4910156B2 (ja) 2006-03-20 2006-12-05 高温形状記憶合金、アクチュエータおよび発動機
EP06833961A EP1997922B1 (fr) 2006-03-20 2006-12-05 Alliage a memoire de forme haute temperature, actionneur et moteur associes
US12/235,528 US20090218013A1 (en) 2006-03-20 2008-09-22 High temperature shape memory alloy, actuator and motor

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US8007604B2 (en) 2006-03-17 2011-08-30 University Of Tsukuba Titanium-tantalum base shape memory alloys, actuator and engine
RU2529472C2 (ru) * 2013-01-10 2014-09-27 Общество с ограниченной ответственностью "Медико-инженерный центр сплавов с памятью формы" Дентальный внутрикостно-поднадкостничный имплантат и способ его установки
KR101614409B1 (ko) 2014-10-27 2016-04-22 한국기계연구원 형상기억합금 및 이의 제조방법
JP2022114989A (ja) * 2021-01-27 2022-08-08 国立研究開発法人物質・材料研究機構 高温形状記憶合金、その製造方法、それを用いたアクチュエータおよびエンジン

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WO2016205781A1 (fr) 2015-06-19 2016-12-22 University Of Florida Research Foundation, Inc. Alliages de nickel-titane, leurs procédés de fabrication et article comprenant ces derniers
US10690123B2 (en) 2017-08-08 2020-06-23 The Boeing Company Cooperative shape memory alloy torque tubes for continuous-action turning motor
CN111020338B (zh) * 2019-12-16 2021-07-30 四川大学 超低温服役镍钛铌形状记忆合金

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8007604B2 (en) 2006-03-17 2011-08-30 University Of Tsukuba Titanium-tantalum base shape memory alloys, actuator and engine
RU2529472C2 (ru) * 2013-01-10 2014-09-27 Общество с ограниченной ответственностью "Медико-инженерный центр сплавов с памятью формы" Дентальный внутрикостно-поднадкостничный имплантат и способ его установки
KR101614409B1 (ko) 2014-10-27 2016-04-22 한국기계연구원 형상기억합금 및 이의 제조방법
JP2022114989A (ja) * 2021-01-27 2022-08-08 国立研究開発法人物質・材料研究機構 高温形状記憶合金、その製造方法、それを用いたアクチュエータおよびエンジン
JP7713215B2 (ja) 2021-01-27 2025-07-25 国立研究開発法人物質・材料研究機構 高温形状記憶合金、その製造方法、それを用いたアクチュエータおよびエンジン

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JPWO2007108180A1 (ja) 2009-08-06
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EP1997922B1 (fr) 2012-06-13
EP1997922A4 (fr) 2011-04-20
EP1997922A1 (fr) 2008-12-03

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